A hydrogen storage system includes a hydrogen storage alloy containment vessel comprising an external pressure containment vessel and a thermally conductive compartmentalization network disposed within the pressure containment vessel. The compartmentalization network creates compartments within the pressure vessel within which a hydrogen storage alloy is disposed. The compartmentalization network includes a plurality of thermally conductive elongate tubes positioned within the pressure vessel forming a coherent, tightly packed tube bundle providing a thermally conductive network between the hydrogen storage alloy and the pressure vessel. The hydrogen storage alloy is a non-pyrophoric AB.sub.2-type Laves phase hydrogen storage alloy having: an A-site to B-site elemental ratio of not more than 0.5; and an alloy composition including (in at %): Zr: 2.0-5.5, Ti: 27-31.3, V: 8.3-9.9, Cr: 20.6-30.5, Mn: 25.4-33.0, Fe: 1.0-5.9, Al: 0.1-0.4, and/or Ni: 0.0-4.0.

A hydrogen storage system includes a hydrogen storage alloy containment vessel comprising an external pressure containment vessel and a thermally conductive compartmentalization network disposed within the pressure containment vessel. The compartmentalization network creates compartments within the pressure vessel within which a hydrogen storage alloy is disposed. One or both of the compartmentalization network and the pressure vessel may be formed by s 3D printing process, such as by Selective Laser Melting (SLM) and/or Direct Metal Laser Sintering (DMLS). The hydrogen storage alloy is a non-pyrophoric AB2— type Laves phase hydrogen storage alloy having: an A-site to B-site elemental ratio of not more than 0.5; and an alloy composition including (in at %): Zr: 2.0-5.5, Ti: 27-31.3, V: 8.3-9.9, Cr: 20.6-30.5, Mn: 25.4-33.0, Fe: 1.0-5.9, Al: 0.1-0.4, and/or Ni: 0.0-4.0.

A hydrogen storage system includes a hydrogen storage alloy containment vessel comprising an external pressure containment vessel and a thermally conductive compartmentalization network disposed within the pressure containment vessel. The compartmentalization network creates compartments within the pressure vessel within which a hydrogen storage alloy is disposed. One or both of the compartmentalization network and the pressure vessel may be formed by s 3D printing process, such as by Selective Laser Melting (SLM) and/or Direct Metal Laser Sintering (DMLS). The hydrogen storage alloy is a non-pyrophoric AB2— type Laves phase hydrogen storage alloy having: an A-site to B-site elemental ratio of not more than 0.5; and an alloy composition including (in at %): Zr: 2.0-5.5, Ti: 27-31.3, V: 8.3-9.9, Cr: 20.6-30.5, Mn: 25.4-33.0, Fe: 1.0-5.9, Al: 0.1-0.4, and/or Ni: 0.0-4.0.

Provided is a hydrogen storage alloy including a ternary alloy of titanium (Ti), iron (Fe), and vanadium (V), wherein V sites in the ternary alloy correspond to some of Ti sites in a binary TiFe alloy including Ti and Fe, and some of Fe sites in the binary TiFe alloy.

A catalyst used for dehydrogenation of an organic hydrogen-storage material to generate hydrogen, a support for the catalyst, and a preparation process thereof are presented. A hydrogen-storage alloy and a preparation process thereof are provided. A process for providing high-purity hydrogen, a high-efficiently distributed process for producing high-purity and high-pressure hydrogen, a system for providing high-purity and high-pressure hydrogen, a mobile hydrogen supply system, and a distributed hydrogen supply apparatus are also described.

A catalyst used for dehydrogenation of an organic hydrogen-storage material to generate hydrogen, a support for the catalyst, and a preparation process thereof are presented. A hydrogen-storage alloy and a preparation process thereof are provided. A process for providing high-purity hydrogen, a high-efficiently distributed process for producing high-purity and high-pressure hydrogen, a system for providing high-purity and high-pressure hydrogen, a mobile hydrogen supply system, and a distributed hydrogen supply apparatus are also described.

A low-cost hydrogen storage material has hydrogen absorption (storage) and desorption properties suitable for hydrogen storage. A hydrogen storage container including the hydrogen storage material and a hydrogen supply apparatus including the hydrogen storage container are disclosed. The hydrogen storage material includes an alloy having a specific elemental composition represented by Formula (1), in which, in a 1000×COMP image of a cross section of the alloy obtained by EPMA, a plurality of phases enriched with R are present, the phases having phase diameters of 0.1 μm or more and 10 μm or less, and 100 or more sets of combinations of two phases in the phases are present in a visual field of 85 μm×120 μm in the COMP image, the shortest separation distance between the two phases being 0.5 to 20 μm.

[Chem. 1]

Ti.sub.(1-a-b)R.sub.aM1.sub.bFe.sub.cMn.sub.dM2.sub.eC.sub.f  (1)

The present disclosure relates to methods for preparing TiMn-based or TiCrMn-based hydrogen storage alloys capable of absorbing and releasing hydrogen. In preferred embodiments the TiMn-based or TiCrMn-based hydrogen storage alloys comprise ferrovanadium (VFc).

A surface treatment method for a hydrogen absorbing alloy powder of the present disclosure is used for a surface treatment on a hydrogen absorbing alloy powder containing rare earth elements and nickel as constituent elements, including an immersion process in which the hydrogen absorbing alloy powder is immersed in an aqueous alkaline solution; and a removal process in which a liquid containing the hydrogen absorbing alloy powder immersed in the aqueous alkaline solution is introduced into a liquid cyclone, and undesired substances having a smaller specific gravity than the hydrogen absorbing alloy powder adhered to the surface of the hydrogen absorbing alloy powder are removed.

A film-shaped fired material of the present invention is a film-shaped fired material 1 which contains sinterable metal particles 10 and a binder component 20, in which a time (A1) after the start of a temperature increase, at which a negative gradient is the highest, in a thermogravimetric curve (TG curve) measured from 40° C. to 600° C. at a temperature-rising-rate of 10° C./min in an air atmosphere and a maximum peak time (B1) in a time range of 0 seconds to 2160 seconds after the start of a temperature increase in a differential thermal analysis curve (DTA curve) measured from 40° C. to 600° C. at a temperature-rising-rate of 10° C./min in an air atmosphere using alumina particles as a reference sample satisfy a relationship of “A1<B1<A1+200 seconds” and a relationship of “A1<2000 seconds”.